Sulfide solid electrolyte

ABSTRACT

A sulfide solid electrolyte that contains lithium, phosphorus, sulfur, chlorine and bromine, wherein in powder X-ray diffraction analysis using CuKα rays, it has a diffraction peak A at 2θ=25.2±0.5 deg and a diffraction peak B at 2θ=29.7±0.5 deg, the diffraction peak A and the diffraction peak B satisfy the following formula (A), and a molar ratio of the chlorine to the phosphorus “c (Cl/P)” and a molar ratio of the bromine to the phosphorus “d (Br/P)” satisfies the following formula (1): 
       1.2&lt; c+d &lt;1.9  (1)
 
       0.845&lt; S   A   /S   B &lt;1.200  (A)
         where S A  is an area of the diffraction peak A and S B  is an area of the diffraction peak B.

TECHNICAL FIELD

The invention relates to a sulfide solid electrolyte.

BACKGROUND ART

In recent years, with rapid spread of information-related equipment orcommunication equipment such as PCs, video cameras, mobile phones, etc.,development of batteries used as the power source thereof is consideredto be important. Among these batteries, a lithium ion battery hasattracted attention due to its high energy density.

In a lithium ion battery that is currently commercially available, sincean electrolyte containing a flammable organic solvent is used,attachment of a safety device that suppresses an increase in temperatureat the time of short circuit, and improvement in structure and materialin order to avoid occurrence of short circuit is required. On the otherhand, it is thought that, since a lithium ion battery obtained byallowing a battery to be totally solid by using a solid electrolyteinstead of liquid electrolyte does not use a flammable organic solventin a battery, simplification of a safety device can be attained, and aproduction cost can be saved or productivity can be improved.

As the solid electrolyte used in a lithium ion battery, a sulfide solidelectrolyte is known. As the crystal structure of a sulfide solidelectrolyte, various structures are known. As one of such crystalstructures, an argyrodite type crystal structure can be given. PatentDocuments 1 to 5 or Non-Patent Documents 1 to 3, etc. disclose anargyrodite type crystal structure comprising one type of a halogen.Further, Non-Patent Documents 4 and 5 report a solid electrolyte havinga composition of Li₆PS₅Cl_(1-x)Br_(x), and disclose an argyrodite typecrystal structure comprising two types of halogen. Some of theargyrodite type crystal structures have high lithium ion conductivity,However, further improvement in ionic conductivity is required. Inaddition, in general, a sulfide solid electrolyte has a problem thatthere is a possibility that it generates hydrogen sulfide when reactedwith moisture contents in air.

RELATED ART DOCUMENTS Patent Documents

-   Patent Document 1: JP-T-2010-540396-   Patent Document 2: WO2015/011937-   Patent Document 3: WO2015/012042-   Patent Document 4: JP-A-2016-24874-   Patent Document 5: WO2016/104702

Non-Patent Documents

0 Non-Patent Document 1: Angew. chem Vol. 47 (2008), No. 4, P. 755-758

-   Non-Patent Document 2: Phys. Status. Solidi Vol. 208 (2011), No.    8, P. 1804-1807-   Non-Patent Document 3: Solid State Ionics Vol. 221 (2012) P. 1-5-   Non-Patent Document 4: Abstract of the 82^(nd) lecture of the    Electrochemical Society of Japan (2015), 2H08-   Non-Patent Document 5: P. 474, 1 H2-50 of the 94^(th) spring annual    meeting proceedings (2014) of the Japan Chemical Society

SUMMARY OF THE INVENTION

One object of the invention is to provide a novel sulfide solidelectrolyte having a further high ionic conductivity.

Further, one object of the invention is to provide a novel sulfide solidelectrolyte in which the amount of hydrogen sulfide generated by areaction with moisture contents in the air is suppressed.

According to one embodiment of the invention, provided is a novelsulfide solid electrolyte that comprises lithium, phosphorus, sulfur,chlorine and bromine, wherein

in powder X-ray diffraction analysis using CuKα rays, it has adiffraction peak A at 2θ=25.2±0.5 deg and a diffraction peak B at2θ=29.7±0.5 deg, the diffraction peak A and the diffraction peak Bsatisfy the following formula (A), and a molar ratio of the chlorine tothe phosphorus “c (Cl/P)” and a molar ratio of the bromine to thephosphorus “d (Br/P)” satisfy the following formula (1):

1.2<c+d<1.9  (1)

0.845<S _(A) /S _(B)<1.200  (A)

-   -   wherein S_(A) is an area of the diffraction peak A and S_(B) is        an area of the diffraction peak B.

According to one embodiment of the invention, an electrode mixcomprising the above-mentioned sulfide solid electrodes and an activematerial is provided.

According to one embodiment of the invention, a lithium ion batterycomprising at least one of the above-mentioned sulfide solid electrodeand the above-mentioned electrode mix is provided.

According to one embodiment of the invention, it is possible to providea sulfide solid electrolyte having a high ionic conductivity.

According to one embodiment of the invention, it is possible to providea sulfide solid electrolyte in which the amount of hydrogen sulfidegenerated by reaction with moisture in the air is suppressed.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a plan view of a cross section of one example of a multi-axialkneader used for production of a sulfide solid electrolyte obtained bycutting at the center of a rotational shaft.

FIG. 2 is a plan view of a cross section of a part where a paddle of therotational shaft is provided of one example of the multi-axial kneaderused for production of a sulfide solid electrode obtained by cuttingperpendicularly to a rotational shaft.

FIG. 3 is an X-ray diffraction pattern of the sulfide solid electrolyteobtained in Example 1.

FIG. 4 is an X-ray diffraction pattern of the sulfide solid electrolyteobtained in Comparative Example 2.

FIG. 5 is an explanatory view of an apparatus used for evaluation of thegeneration of hydrogen sulfide of the sulfide solid electrolyte.

FIG. 6 show the results of the structural analysis by the synchrotronradiation of the sulfide solid electrolyte obtained in Example 1.

MODE FOR CARRYING OUT THE INVENTION

The sulfide solid electrolyte according to one embodiment of theinvention comprises lithium (Li), phosphorus (P), sulfur (S), chlorine(CI) and bromine (Br) as constituent elements, and is characterized inthat it has a diffraction peak A at 2θ=25.2±0.5 deg and a diffractionpeak B at 2θ=29.7±0.5 deg and the diffraction peak A and the diffractionpeak B satisfy the following formula (A):

0.845<S _(A) /S _(B)<1.200  (A)

wherein in the formula, S_(A) is an area of the diffraction peak A andS_(B) is an area of the diffraction peak B.

The diffraction peak A and the diffraction peak B are peaks derived froman argyrodite type crystal structure. In addition to the diffractionpeak A and the diffraction peak B, a diffraction peak derived from anargyrodite type crystal structure may appear at 2θ=15.3±0.5 deg,17.7±0.5 deg, 31.1±0.5 deg, 44.9±0.5 deg or 47.7±0.5 deg, for example.The sulfide solid electrolyte of this embodiment may have these peaks.

In this embodiment, the position of the diffraction peak is judged to beA±0.5 deg assuming that the median value is A. A is preferably A±0.3deg. For example, in the case of the above-mentioned diffraction peak of2θ=25.2±0.5 deg. the median value A is 25.2 deg and is preferablypresent in a range of 2θ=25.2±0.3 deg. The same can be applied tojudgement of all of the other diffraction peak positions in theinvention.

By satisfying the above formula (A), the sulfide solid electrolyte ofthis embodiment has a higher ionic conductivity as compared with theconventional argyrodite type crystal structure-containing solidelectrolyte. The above formula (A) means that the area ratio of thediffraction peaks (S_(A)/S_(B)) is larger than that of the conventionalargyrodite type crystal structure-containing solid electrolyte. It ispreferred that the area ratio (S_(A)/S_(B)) be 0.850 or more and 1.150or less, with 0.860 or more and 1.100 or less being more preferable.

The fact that the area ratio (S_(A)/S_(B)) is large means that the ratioof a halogen (the total of Cl and Br) occupying a site of the argyroditetype crystal structure is high. Especially, the site occupation ratio ofBr is increased as compared with that of the conventional technology. Ingeneral, various types of crystal components and amorphous componentsare present in mixture in a sulfide solid electrolyte. Part of Cl and Brthat is incorporated as constituent elements of the sulfide solidelectrolyte forms the argyrodite type crystal structure, and theremaining Cl and Br form a crystal structure other than the argyroditetype crystal structure and an amorphous component. It is thought thatthere is a possibility that the remaining Cl and Br are contained inremaining raw materials. This embodiment is based on a finding that, byincreasing a halogen occupying the site in the argyrodite type crystalstructure, especially, by increasing the site occupation ratio of Br ascompared with that of the conventional technology, the area ratio(S_(A)/S_(B)) becomes large, whereby the ionic conductivity of thesulfide solid electrolyte is increased.

The argyrodite type crystal structure is a structure in which a PS₄ ³⁻structure is a main unit structure of the skeleton and a site in thevicinity of this structure is occupied by S and a halogen (Cl, Br)surrounded by Li.

The area ratio of the X-ray diffraction peak of the crystal structurecan be calculated from the coordinates of each element of the crystalstructure (see “XRD diffraction handbook”, third edition, Rigaku DenkiCo., 2000, p. 14-15). A common argyrodite type crystal structure is acrystal structure indicated by a space group F-43M and is shown by No.216 of the data base of International Tables for Crystallography VolumeG: Definition and exchange of crystallographic data (ISBN:978-1-4020-3138-0). In the crystal structure shown by No. 216, a 4a siteand a 4d site are present around the PS₄ ³⁻ structure, an element havinga large ionic radius tends to occupy the 4a site, and an element havinga small ionic radius tends to occupy the 4d site.

In the unit lattice of the argyrodite type crystal structure, there areeight 4a sites and 4d sites in total. For a case in which four Cls andfour Ss are arranged in these sites (Case 1), and a case in which fourCls, two Brs and two Ss are arranged in these sites (Case 2), an arearatio of an X-ray diffraction peak was calculated. As a result, in Case2, as compared with Case 1, while the area of the diffraction peak A(diffraction peak at 2θ=25 deg) becomes broad, only a small change isobserved in the area of the diffraction peak B (diffraction peak at2θ=30 deg). From the above calculation results, it is considered that,due to occupation of the site by Br, the area ratio (S_(A)/S_(B))becomes large.

In general, the area ratio and the intensity ratio of the X-raydiffraction peak are proportional to the number of electrons of theelement (see “X-ray crystal analysis guide”, Shokabo (1983)). It isassumed that, since CI and S have roughly the same electron number andBr has a larger number of electrons, it is considered that the siteoccupation ratio of Br in the crystal diffraction plane corresponding tothe diffraction peak A is increased. In view of the ionic radius,occupation ratio in the 4a site is especially increased.

Increasing the amount of a halogen occupying the site in the argyroditetype crystal structure means that the amount of S occupying the site inthe argyrodite type crystal structure is relatively reduced. A halogenhaving a valence of −1 has a force weaker to attract Li than S having avalence of −2. Further, the number of Li attracted is small. It isassumed that the density of Li in the vicinity of the site is decreased,and Li tends to move easily, whereby the ionic conductivity of theargyrodite type crystal structure is increased.

When the halogen is Cl alone, the occupation ratio of S increases at the4a site. By using Br having the equivalent ionic radius to that of Swith Cl, the occupation ratio of Br in the 4a site is increased, and asa result, the entire halogen occupation ratio is improved. In addition,even when Cl occupies some 4a sites, Cl at the 4a site is unstable andmay be desorbed during a heat treatment. Therefore, it is thought thatit is preferable not only to simply increase the halogen occupationratio but also to occupy a suitable site for a halogen having a suitableionic radius. In this embodiment, it is assumed that the ionicconductivity is increased since a large amount of two halogens (Cl andBr) appropriately occupy the site in the argyrodite type crystalstructure.

In this embodiment, a molar ratio of the chlorine to the phosphorus “c(Cl/P)” and a molar ratio of the bromine to the phosphorus “d (Br/P)”satisfy the following formula (1):

1.2<c+d<1.9  (1)

c+d is a molar ratio of the chlorine and the bromine to the phosphorus.By allowing the c+d to be in the above-mentioned range, the effect ofimproving the ionic conductivity of the sulfide solid electrolyte isincreased. c+d is preferably 1.4 or more and 1.8 or less, with 1.5 ormore and 1.7 or less being more preferable.

In the sulfide solid electrolyte according to one embodiment of theinvention, a molar ratio of the bromine to the phosphorus “d (Br/P)” ispreferably 0.15 or more and 1.6 or less. The molar ratio “d” is furtherpreferably 0.2 or more and 1.2 or less, with 0.4 or more and 1.0 or lessbeing more preferable.

It is preferred that the molar ratio of the chlorine to the phosphorus“c (Cl/P)” and the molar ratio of the bromine to the phosphorus “d(Br/P)” satisfy the following formula (2):

0.08<di(c+d)<0.8  (2)

d/(c+d) is more preferably 0.15 or more and 0.6 or less, with 0.2 ormore and 0.5 or less being further preferable.

Further, it is preferred that the molar ratio of the lithium to thephosphorus “a (Li/P)”, the molar ratio of the sulfur to the phosphorus“b (SIP)”, the molar ratio of the chlorine to the phosphorus “c (Cl/P)”and the molar ratio of the bromine to the phosphorus “d (Br/P)” satisfythe following formulas (3) to (5):

5.0≤a≤7.5  (3)

6.5≤a+c+d≤7.5  (4)

0.5≤a−b≤1.5  (5)

provided that b>0, c>0 and d>0.

By satisfying the above formulas (3) to (5), the argyrodite type crystalstructure tends to be formed easily.

The above formula (3) is preferably 5.0≤a≤6.8, with 5.2≤a≤6.6 being morepreferable.

The above formula (4) is preferably 6.6≤a+c+d≤7.4, with 6.7≤a+c+d≤7.3being more preferable.

The above formula (5) is preferably 0.6≤a−b≤1.3, with 0.7≤a−b≤1.3 beingmore preferable.

Within a range that does not impart the advantageous effects of theinvention, in addition to Li, P, S, Cl and Br mentioned above, thesulfide solid electrolyte of this embodiment may contain Si, Ge, Sn, Pb,B, Al, Ga, As, Sb, Bi, O, Se, Te or the like. The sulfide solidelectrolyte may essentially consist only of Li, P, S, Cl and Br. The“essentially consist of Li, P, S, Cl and Br” means that the sulfidesolid electrolyte comprises only Li, P, S, Cl and Br, except forinevitably mixed in impurities.

The molar ratio and composition of each element mentioned above is not amolar ratio and composition of raw materials used in production, but amolar ratio and composition in the sulfide solid electrolyte as a formedproduct. The molar ratio of each element can be controlled by adjustingthe content of each element in the raw material.

In the invention, as the molar ratio and composition of each element inthe sulfide solid electrolyte, a value measured by an ICP emissionspectrometry is used, except for cases where an analysis is difficult.The methods for measurement are described in the Examples.

As for the sulfide solid electrolyte according to one embodiment of theinvention, it is preferred that the sulfide solid electrolyte do nothave a diffraction peak derived from lithium halide in powdery X-raydiffraction using CuKα rays. If it has a peak derived from lithiumhalide, it is preferred that the following formula (B) is satisfied:

0<I _(C) /I _(A)<0.08  (B)

wherein I_(C) is an intensity of a diffraction peak of the lithiumhalide and I_(A) is an intensity of a diffraction peak at 2θ=25.2±0.5deg.

The above formula (B) shows that the amount of lithium halide isrelatively small as compared with the amount of the argyrodite typecrystal structure. Presence of lithium halide means presence of ahalogen that does not occupy the site in the argyrodite type crystalstructure among all halogens in the sulfide solid electrolyte.

The intensity I_(C) of the diffraction peak of lithium halide is theintensity of a diffraction peak that appears in a range of 34.0deg≤2θ≤35.5 deg when the lithium halide is LiCl. However, if two or morediffraction peaks are present in this range, the intensity is anintensity of a diffraction peak that appears at the highest angle side.In the case of LiBr, I_(C) is the intensity of a peak that appearswithin a range of 32.5 deg≤2θ≤33.9 deg. However, if two or morediffraction peaks are present in this range, I_(C) is the intensity of apeak that appears at the smallest angle side. The reason for suchdefinition is as follows. If a novel crystal structure including ahalogen mentioned later is present, a diffraction peak appears at14.4±0.5 deg and 33.8±0.5 deg. When only one diffraction peak isobserved in a range of 32.5 deg≤2θ≤35.5 deg in spite of a fact that adiffraction peak is observed at 14.4±0.5 deg, it is assumed that thesediffraction peaks are derived from a novel crystal structure including ahalogen, mentioned later. In this case, it is thought that a diffractionpeak derived from lithium halide does not appear. When diffraction peaksof LiCl and LiBr are observed, the I_(C) is the total of thesediffraction peaks.

The formula (B) is more preferably 0<I_(C)/I_(A)<0.07, with0<I_(C)/I_(A)<0.06 being further preferable.

It is preferred that in powdery X-ray diffraction using CuKα rays, thesulfide solid electrolyte according to one embodiment of the inventiondo not have a diffraction peak at 2θ=14.4±0.5 deg and 33.8±0.5 deg. Ifit has a diffraction peak, it is preferred that the following formula(C) be satisfied.

0<I _(D) /I _(A)<0.09  (C)

wherein I_(D) is an intensity of a diffraction peak at 2θ=14.4±0.5 degand I_(A) is an intensity of a diffraction peak at 2θ=25.2±0.5 deg.

It is assumed that the crystal having a diffraction peak at 2θ=14.4±0.5deg and 33.8±0.5 deg is novel, and is a structure that partiallycontains a halogen. The above formula (C) means that the amount of thenovel crystal structure is relatively small as compared with theargyrodite type crystal structure. Presence of the novel crystalstructure means presence of a halogen that does not occupy the site inthe argyrodite type crystal structure among all halogens in the sulfidesolid electrolyte.

It is more preferable that the formula (C) is 0<I_(D)/I_(A)<0.06, with0<I_(C)/I_(D)<0.05 being further preferable.

In the sulfide solid electrolyte according to one embodiment of theinvention, it is preferred that the lattice constant of the argyroditetype crystal structure be 9.800 Å or more and 9.920 Å or less.

The fact that the lattice constant of the argyrodite type crystalstructure is small implies that the amount of chlorine and brominecontained in the crystal structure is large. When it is less than 9.800Å, it is considered that bromine is difficult to be incorporated intothe crystal structure.

The lattice constant of the argyrodite type crystal structure iscalculated from the XRD pattern obtained by X-ray diffractionmeasurement (XRD) by analyzing whole pattern fitting (WPF) by usingcrystal structure analysis software. Details of the measurement areshown in the Examples.

In the sulfide solid electrolyte according to one embodiment of theinvention, in the solid ³¹P-NMR measurement, it is preferred that thesolid electrolyte have a peak at each of 81.5 to 82.5 ppm (hereinafter,referred to as the first region), 83.2 to 84.7 ppm (hereinafter,referred to as the second region), 85.2 to 86.7 ppm (hereinafter,referred to as the third region) and 87.2 to 89.4 ppm (hereinafter,referred to as the fourth region), and it is preferred that the ratio ofthe sum of the area of the peak at 81.5 to 82.5 ppm and 83.2 to 84.7 ppmrelative to the total of all peaks that appear within a range of 78 to92 ppm be 60% or more. It is assumed that the fact that the ratio of thesum of the area of the first peak and the second peak is high means thatthe sum of the amount of chlorine and the amount of bromine incorporatedinto the argyrodite type crystal structure is large. As a result, theionic conductivity of the solid electrolyte is increased.

Meanwhile, the peak in the first region is referred to as the first peak(P₁), the peak in the second region is referred to as the second peak(P₂), the peak in the third region is referred to as the third peak (P₃)and the peak in the fourth region is referred to as the fourth peak(P₄).

Presence of a peak in a region means that a peak having a peak top inthe region is present or a peak is present in this region at the time ofseparation by the non-linear least squares method.

Due to the difference in the distribution of free chlorine (Cl) and freesulfur (S) around the PS₄ ³⁻ structure in the crystal, the argyroditetype crystal structure (Li₆PS₅Cl) in which the halogen is chlorine, inits solid ³¹P-NMR spectrum, resonance lines of phosphorus differing inchemical shift are observed in an overlapped manner (Non-Patent Document1). Based on these findings, the inventors examined the solid ³¹P-NMRspectrum of the argyrodite type crystal structure in which the ratio ofa free halogen and a free sulfur is different. As a result, it was foundthat the NMR signal observed in the region of 78 to 92 ppm can beseparated into four kinds of PS₄ ³⁻ structure peaks with differentdistribution states of surrounding free S and free halogen. Further, itwas found that among the four kinds of peaks, if the ratio of areas ofpeaks closer to the high magnetic field side (the sum of the first peakand the second peak mentioned above) is high, the ionic conductivity ofthe solid electrolyte is high. It is assumed that the first peak and thesecond peak mentioned above are derived from a PS₄ ³⁻ structure in whichmany of surrounding free elements are CI or Br. On the other hand, it isassumed that the third peak and the fourth peak mentioned above arederived from a PS₄ ³⁻ structure in which many of surrounding freeelements are S.

The sulfide solid electrolyte according to one embodiment of theinvention can be produced by a production method comprising a step, forexample, in which a mixture of raw materials is reacted by applying amechanical stress to prepare an intermediate and a step in which theintermediate is heat-treated for crystallization.

As the raw materials used, two or more compounds or simple substancescontaining, as a whole, elements to be contained as essential componentsin a sulfide solid electrolyte i.e. lithium, phosphorus, sulfur,chlorine and bromine are used in combination.

Examples of the raw material containing lithium include lithiumcompounds such as lithium sulfide (Li₂S), lithium oxide (Li₂O), lithiumcarbonate (Li₂CO₃), lithium metal simple substance, and the like. Amongthem, a lithium compound is preferable, with lithium sulfide being morepreferable.

The lithium sulfide mentioned above can be used without specificrestrictions. However, one having a high purity is preferable. Lithiumsulfide can be produced by a method described in JP-A-H07-330312,JP-A-H09-283156, JP-A-2010-163356, JP-A-2011-84438, or the like.

Specifically, lithium hydroxide and hydrogen sulfide are reacted in ahydrocarbon-based organic solvent at 70° C. to 300° C. to form lithiumhydrosulfide, and subsequently, hydrogen sulfide is removed from thisreaction liquid, thereby to produce lithium sulfide (JP-A-2010-163356).

Further, by reacting lithium hydroxide and hydrogen sulfide in anaqueous solvent at 0° C. to 100° C. to form lithium hydrosulfide, andsubsequently, hydrogen sulfide is removed from this reaction liquid,thereby to produce lithium sulfide (JP-A-2011-84438).

Examples of the raw material containing phosphorus include phosphoruscompounds such as phosphorus sulfide such as phosphorus trisulfide(P₂S₃) and phosphorus pentasulfide (P₂S₅), and sodium phosphate(Na₃PO₄), phosphorus simple substance or the like. Among these,phosphorus sulfide is preferable, with phosphorus pentasulfide (P₂S₅)being more preferable. As for the phosphorus compounds and thephosphorus simple substance, any can be used without specificrestrictions as long as they are commercially available.

As the raw material containing chlorine and/or bromine, it is preferredthat the raw material contain a halogen compound represented by thefollowing formula (6), for example.

M_(l)-X_(m)  (6)

In the formula (6), M is sodium (Na), lithium (Li), boron (B), aluminum(Al), silicon (Si), phosphorus (P), sulfur (S), germanium (Ge), arsenic(As), selenium (Se), tin (Sn), antimony (Sb), tellurium (Te), lead (Pb),bismuth (Bi) or those in which an oxygen element or a sulfur element arebonded to these elements, and lithium (Li) or phosphorus (P) ispreferable with lithium (Li) being more preferable.

X is chlorine (CI) or bromine (Br).

I is an integer of 1 or 2 and m is an integer of 1 to 10. When m is 2 to10, that is, when plural Xs are present, the Xs may be the same ordifferent. For example, in the case of SiBrCl₃ mentioned later, m is 4,and X is formed of different elements, i.e. Br and Cl.

As the halogen compound represented by the formula (6), NaCl, NaBr,LiCl, LiBr, BCl₃, BBr₃, AlBr₃, AlCl₃, SiCl₄, SiCl₃, Si₂Cl₆, SiBr₄,SiBrCl₃, SiBr₂Cl₂, PCl₃, PCl₅, POCl₃, PBr₃, POBr₃, P₂Cl₄, SCl₂, S₂Cl₂,S₂Br₂, GeCl₄, GeBr₄, GeCl₂, GeBr₂, AsCl₃, AsBr₃, SeCl₂, SeCl₄, Se₂Br₂,SeBr₄, SnCl₄, SnBr₄, SnCl₂, SnBr₂, SbCl₃, SbBr₃, SbCl₅, TeCl₂, TeCl₄,TeBr₂, TeBr₄, PbCl₄, PbCl₂, PbBr₂, BiCl₃, BiBr₃ or the like can begiven.

Among these, lithium chloride (LiCl), lithium bromide (LiBr), phosphoruspentachloride (PCl₅), phosphorus trichloride (PCl₃), phosphoruspentabromide (PBrs), phosphorus tribromide (PBr₃) or the like canpreferably be given. Among these, LiCl, LiBr or PBr₃ are preferable,with LiCl and LiBr being further preferable.

As the halogen compound, one of the above-mentioned compounds may beused singly, or two or more may be used in combination, That is, atleast one of the above-mentioned compounds can be used.

In one embodiment of the invention, it is preferred that the rawmaterials contain a lithium compound, a phosphorus compound and ahalogen compound. It is preferred that at least one of the lithiumcompound and the phosphorus compound comprises a sulfur element.Combination of Li₂S, phosphorus sulfide, LiCl and LiBr is morepreferable, with combination of Li₂S, P₂S₅, LiCl and LiBr being furtherpreferable.

When Li₂S, P₂S₅, LiCl and LiBr are used as the raw material of thesulfide solid electrolyte, the molar ratio of the raw materialsincorporated can be Li₂S:P₂S₅:total of LiCl and LiB+30 to 60:10 to 25:15to 50.

In one embodiment of the invention, a mechanical stress is applied tothe above-mentioned raw materials to allow them to react, therebyallowing them to be an intermediate. Here, the “applying a mechanicalstrength” means that shear force, impact strength, etc. are mechanicallyapplied. As means for applying a mechanical stress, a pulverizer such asa planetary ball mill, a vibration mill and a rolling mill, a kneader,etc. can be given.

In the conventional technology (for example, Patent Document 2, etc.),pulverization and mixing are carried out to such an extent that thecrystallinity of the raw material powder can be maintained. On the otherhand, in this embodiment, it is preferable that the raw materials besubjected to a mechanical stress and reacted, thereby to obtain anintermediate containing a glass component. That is, by a mechanicalstress higher than that used in the conventional technology,pulverization and mixing are conducted to such a level that at leastpart of the raw material powder cannot maintain crystallinity. As aresult, in the stage of an intermediate, a PS₄ structure that is a basicskeleton of the argyrodite type crystal structure can be generated and ahalogen can be highly dispersed. It is assumed that a halogen that ishighly dispersed in an intermediate is efficiently introduced into asite of the argyrodite type crystal structure by heat treatment. As aresult, it is assumed that the sulfide solid electrolyte of thisembodiment exhibits high ionic conductivity.

Presence of a glass (amorphous) component in an intermediate can beconfirmed by the presence of a broad peak (hallo pattern) derived froman amorphous component in an XRD measurement.

As the condition of pulverization and mixing, for example, when aplanetary ball mill is used as a pulverizer, the rotation speed may befrom several tens to several hundreds of revolution/minute and may betreated for 0.5 hour to 100 hours. More specifically, in the case of theplanetary ball mill (Model No, P-7, manufactured by Fritsch Co.) used inthe Examples, the rotation speed of the planetary ball mill ispreferably 350 rpm or more and 400 rpm or less, more preferably 360 rpmor more and 380 rpm or less.

For example, when a ball made of zirconia is used as the pulverizationmedia, its diameter is preferably 0.2 to 20 mm.

The intermediate prepared by pulverizing and mixing is heat-treated. Theheat treatment temperature is preferably 350 to 480° C., furtherpreferably 360 to 460° C., with 380 to 450° C. being more preferable. Byallowing the heat treatment temperature to be slightly slower than thatused in conventional technologies, a halogen contained in the argyroditetype crystal structure tends to be increased. As for the reason, it isassumed that, if the heat treatment temperature is high, a halogen tendsto be removed easily from a site in the argyrodite type crystalstructure.

Although the atmosphere of the heat treatment is not particularlylimited, it is preferred that the atmosphere be not a hydrogen sulfidestream but an inert gas atmosphere such as nitrogen or argon. It isassumed that by suppressing substitution of free halogen in the crystalstructure with sulfur, the amount of halogen in the crystal structurecan be increased, and as a result, the ion conductivity of the obtainedsulfide solid electrolyte is improved.

When a kneader is used as the means for applying the above-mentionedmechanical stress, the kneader is not particularly restricted. However,in respect of easiness in production, a multi-axial kneader having twoor more shafts is preferable.

As the multi-axial kneader, for example, one provided with a casing, twoor more rotational shafts that are arranged such that they penetrate thecasing in the longitudinal direction and a paddle (screw) is providedalong the axial direction, and a raw material supply port at one end inthe longitudinal direction of the casing and a discharge port at theother end can be given. No other configurations are not particularlyrestricted as long as two or more rotational movements are mutuallyacted to generate a mechanical stress. By rotating the two or morerotational shafts in which two or more paddles are provided, two or morerotational movements are mutually acted such that a mechanical stresscan be formed, whereby the raw materials can be reacted by themechanical stress that is applied to the raw materials moving from thesupply port to the discharge port along the rotational shaft.

One preferable example of the multi-axial kneader that can be used inone embodiment of the invention will be explained with reference to FIG.1 and FIG. 2. FIG. 1 is a plan view of a cross section of themulti-axial kneader obtained by cutting at the center of the rotationalshaft, and FIG. 2 is a plan view of a cross section of a part where apaddle of the rotational shaft is provided of the multi-axial kneaderobtained by cutting perpendicularly to a rotational shaft.

The multi-axial kneader shown in FIG. 1 is a bi-axial kneader providedwith a casing 1 provided with a supply port 2 at its one end and adischarge port 3 at the other end, two rotational shafts 4 a and 4 barranged such that they penetrate in the longitudinal direction of thecasing 1. In each of the rotational shafts 4 a and 4 b, a paddle 5 a anda paddle 5 b are provided. The raw materials enter the casing 1 throughthe supply port 2, and are reacted by application of a mechanical stressin the paddle 5 a and the paddle 5 b. The resulting reaction product isdischarged from a discharge port 3.

The number of the rotational shaft 4 is not particularly restricted, aslong as it is two or more. In respect of multiplicity of use, two tofour rotational shafts are preferable, and two rotational shafts aremore preferable. Further, the rotational shaft 4 may preferably beparallel shafts that are in parallel with each other.

The paddle 5 is provided on the rotational shaft in order to knead theraw materials, and is also called a “screw”. No specific restrictionsare imposed on the cross sectional shape. In addition to an approximatetriangle shown in FIG. 2 in which each side of an equilateral triangleis uniformly projected arc-shaped, circular, elliptical, substantiallyquadrangular and the like can be given, and a shape in which a notch isprovided in a part of these shapes as a base can also be given.

In the case of providing a plurality of paddles, as shown in FIG. 2,each paddle may be provided on the rotating shaft at different angles.In addition, when trying to obtain more kneading effects, the meshingtype paddle may be selected.

Although the number of rotations of the paddle is not particularlylimited, it is preferably 40 to 300 rpm, more preferably 40 to 250 rpm,and further preferably 40 to 200 rpm.

In the multi-axial kneader, a screw 6 may be provided on the supply port2 side as shown in FIG. 1 so that the raw materials are supplied to thekneader without any delay. A reverse screw 7 may be provided on thedischarge port 3 side as shown in FIG. 1 so that the reactant obtainedvia the paddle 5 do not retain in the casing.

As a multi-axial kneader, a commercially available kneading machine canalso be used. Examples of commercially available multi-axial kneadingmachines include KRC kneader (manufactured by Kurimoto Co., Ltd.) andthe like.

The kneading time of the raw materials varies depending on the type ofthe element constituting the sulfide solid electrolyte to be obtained,the composition ratio, and the temperature during the reaction, and maybe adjusted as appropriate, preferably 5 minutes to 50 hours, morepreferably 10 minutes to 15 hours, and further preferably 1 to 12 hours.

The kneading temperature of the raw materials varies depending on thetype of the element constituting the sulfide solid electrolyte to beobtained, the composition ratio, and the time during the reaction, so itmay be appropriately adjusted, preferably 0° C. or more, more preferably25° C. or more, more preferably 100° C. or more, and most preferably250° C. or more. When the temperature is high, the argyrodite typecrystal structure tends to be precipitated more easily at the time ofkneading. If it is 350° C. or higher, it is considered that theargyrodite type crystal structure is more likely to be precipitated. Theupper limit of the kneading temperature may be such that the generatedargyrodite type crystal structure is not decomposed, that is, it is lessthan 500′C.

The intermediate discharged from the discharge pod of the multi-axialkneader may be supplied from the supply port again in accordance withthe degree of the progress of the reaction, and a reaction may furtherproceed. The degree of the progress of the reaction can be grasped froman increase or decrease of the peak derived from the raw materials ofthe resulting intermediate.

By subjecting the intermediate obtained by kneading to a heat treatment,whereby a sulfide solid electrolyte is obtained. The heat treatmenttemperature is preferably 350 to 480° C., further preferably 360 to 460°C., with 380 to 450° C. being more preferable. The atmosphere of theheat treatment is not particularly restricted, but is preferably aninert gas atmosphere such as nitrogen and argon, not a stream ofhydrogen sulfide.

The sulfide solid electrolyte of the invention can be used in a solidelectrolyte layer, a positive electrode, a negative electrode, etc. of alithium ion secondary battery.

[Electrode Mix]

The electrode mix according to one embodiment of the invention comprisesthe sulfide solid electrolyte of the invention mentioned above and anactive material, or is produced from the sulfide solid electrolyte ofthe invention. When a negative electrode active material is used as anactive material, the electrode mix becomes a negative electrode mix. Onthe other hand, when a positive electrode active material is used, itbecomes a positive electrode mix.

Negative Electrode Mix

A negative electrode mix is obtained by incorporating a negativeelectrode material to the sulfide solid electrolyte of the invention.

As the negative electrode active material, a carbon material, a metalmaterial, etc. can be used. A composite material formed of two or moreof these can also be used. Further, a negative electrode material thatwill be developed in the future can be used.

It is preferred that the negative active material have electronconductivity.

The carbon materials include graphite (e.g., artificial graphite),graphite carbon fiber, resin calcined carbon, pyrolytic vapor-growncarbon, coke, mesocarbon microbeads (MCMB), burned carbon of furfurylalcohol resin, polyacene, pitch type carbon fibers, vapor grown carbonfibers, natural graphite, non-graphitizable carbon and the like can begiven.

Examples of the metallic material include a simple metal substance,alloys, and metal compounds. As the simple metal substance, metalsilicon, metal tin, metal lithium, metal indium, metal aluminum can bementioned. As the alloy, an alloy containing at least one of silicon,tin, lithium, indium and aluminum can be mentioned. As the metalcompound, a metal oxide can be mentioned. The metal oxide is, forexample, silicon oxide, tin oxide, aluminum oxide.

The blending ratio of the negative electrode active material and thesolid electrolyte is preferably the negative electrode active materialthe solid electrolyte=95 wt %:5 wt % to 5 wt %:95 wt %, more preferably90 wt %:10 wt % to 10 wt %:90 wt %, and further preferably 85 wt %:15 wt% to 15 wt %:85 wt %.

When the content of the negative electrode active material in thenegative electrode mix is too small, the electric capacity becomessmall. In addition, when the negative electrode active material haselectron conductivity and does not contain a conductive assistant orcontains only a small amount of a conductive assistant, it is consideredthat electron conductivity (electron conduction path) in the negativeelectrode decreases and the rate characteristics may be lowered. Or, theutilization factor of the negative electrode active material isdecreased, whereby the electric capacity may be decreased. On the otherhand, if the content of the negative electrode active material in thenegative electrode mix is too large, it is considered that the ionicconductivity (ion conduction path) in the negative electrode may belowered to decrease the rate characteristics, or the utilization factorof the negative electrode active material may be lowered to decrease theelectronic capacity.

The negative electrode mix may further contain a conductive assistant.

When the negative electrode active material has low electronicconductivity, it is preferable to add a conductive assistant. Theconductive assistant is sufficient if it has conductivity, and itselectron conductivity is preferably 1×10³S/cm or more, more preferably1×10⁵S/cm or more.

As specific examples of preferable conductive assistant, a carbonmaterial, a material including at least one element selected fromnickel, copper, aluminum, indium, silver, cobalt, magnesium, lithium,chromium, gold, ruthenium, platinum, beryllium, iridium, molybdenum,niobium, osmium, rhodium, tungsten, and zinc, more preferably a carbonsimple substance having high conductivity, a carbon material other thansimple substance of carbon; simple substances, mixtures or compoundsincluding nickel, copper, silver, cobalt, magnesium, lithium, ruthenium,gold, platinum, niobium, osmium or rhodium, can be given.

Specific examples of the carbon material include carbon black such asKetjen black, acetylene black, denka black, thermal black, and channelblack; graphite, carbon fiber, activated carbon and the like, which maybe used alone or in combination of two or more. Among them, acetyleneblack, denka black, and Ketjen black having high electronic conductivityare preferable.

In the case where the negative electrode mix contains a conductiveassistant, the content of the conductive assistant in the compositematerial is preferably 1 to 40% by mass, more preferably 2 to 20% bymass. If the content of the conductive assistant is too small, it isconsidered that the electronic conductivity of the negative electrodemay be lowered to deteriorate the rate characteristics, and theutilization factor of the negative electrode active material may bedecreased to lower the electric capacity. On the other hand, if thecontent of the conductive assistant is too large, the amount of thenegative electrode active material and/or the amount of the solidelectrolyte decreases. It is presumed that the electric capacitydecreases as the amount of the negative electrode active materialdecreases. Further, if the amount of the solid electrolyte decreases, itis considered that the ionic conductivity of the negative electrode maybe lowered, thereby to lower the rate characteristics, or theutilization factor of the negative electrode active material may belowered to decrease the electric capacity.

In order to allow the negative electrode active material and the solidelectrolyte to be bonded tightly, a binder may be further included.

As the binder, fluorine-containing resins such aspolytetrafluoroethylene (PTFE), polyvinylidene fluoride (PVDF), fluorinerubber and the like, thermoplastic resins such as polypropylene andpolyethylene, ethylene-propylene-diene rubber (EPDM), sulfonated EPDM,natural butyl rubber (NBR) and the like can be used alone or as amixture of two or more kinds. It is also possible to use an aqueousdispersion of a cellulose type or SBR, which are aqueous binders, or thelike.

The negative electrode mix can be produced by mixing a solid electrolyteand a negative electrode active material, and an arbitrary conductiveassistant and/or a binder.

There are no particular restrictions on the mixing method, but it ispossible to use, for example, dry mixing by mixing using a mortar, aball mill, a bead mill, a jet mill, a planetary ball mill, a vibratingball mill, a sand mill, a cutter mill; and wet mixing in which, afterdispersing the raw materials in an organic solvent, mixing is conductedwith a mortar, a ball mill, a bead mill, a planetary ball mill, avibration ball mill, a sand mill, and a film mix, followed by removal ofthe solvent. Among them, wet mixing is preferable in order not todestroy the negative electrode active material particles.

Positive Electrode Mix

A positive electrode mix can be obtained by blending a positiveelectrode active material with the solid electrolyte of the invention.

A positive electrode active material is a material into which a lithiumion can be inserted and from which a lithium ion can be removed, and onethat is known as the positive electrode active material in the field ofa battery can be used. Further, a positive electrode active materialthat will be developed in the future can be used.

Examples of the positive electrode active material include metal oxides,sulfides, and the like. Sulfides include metal sulfides and non-metalsulfides.

The metal oxide is, for example, a transition metal oxide. Specifically,V₂O₅, V₆O₁₃, LiCoO₂, LiNiO₂, LiMnO₂, LiMn₂O₄, Li(Ni_(a)Co_(b)Mn_(c))O₂(here, 0<a<1, 0<b<1, 0<c<1, a+b+c=1), LiNi_(1-Y)Co_(Y)O₂,LiCo_(1_Y)Mn_(Y)O₂, LiNi_(1-Y)Mn_(Y)O₂ (here, 0≤Y<1),Li(Ni_(a)Co_(b)Mn_(c))O₄ (0<a<2, 0<b<2, 0<c<2, a+b+c=2),LiMn_(2-Z)Ni_(Z)O₄, LiMn_(2-Z)Co_(Z)O₄ (here, 0<Z<2), LiCoPO₄, LiFePO₄,CuO, Li(Ni_(a)Co_(b)Al_(c))O₂ (here, 0<a<1, 0<b<1, 0<c<1, a+b+c=1) Orthe like can be given.

Examples of the metal sulfide include titanium sulfide (TiS₂),molybdenum sulfide (MoS₂), iron sulfide (FeS, FeS₂), copper sulfide(CuS), nickel sulfide (Ni₃S₂) and the like.

In addition to these, bismuth oxide (Bi₂O₃), bismuth lead (Bi₂Pb₂O₅) andthe like can be mentioned as the metal oxide.

Examples of nonmetallic sulfides include organic disulfide compounds andcarbon sulfide compounds.

In addition to those mentioned above, niobium selenide (NbSe₃), metalindium, sulfur also be used as the positive electrode active material.

The positive electrode mix may further comprise a conductive assistant.

The conductive assistant is the same as that of the negative electrodemix.

The blending ratio of the solid electrode and the positive electrodeactive material of the positive electrode mix, the content of theconductive assistant and the method for producing the positive electrodemix are the same as those of the above-mentioned negative electrode mix.

[Lithium Ion Battery]

The lithium ion battery according to one embodiment of the inventioncomprises at least one of the above-mentioned sulfide solid electrolyteand the electrode mix of the invention, or is produced from at least oneof the sulfide solid electrolyte and the electrode mix.

The configuration of the lithium ion battery is not particularlyrestricted, but it has a structure in which a negative electrode layer,an electrolyte layer and a positive electrode layer are stacked in thisorder. Hereinbelow, an explanation will be made on each layer of thelithium ion battery.

(1) Negative Electrode Layer

The negative electrode layer is preferably a layer that is produced fromthe negative electrode mix of the invention.

Alternatively, the negative electrode layer is a layer that comprisesthe negative electrode mix of the invention.

The thickness of the negative electrode layer is preferably 100 nm ormore and 5 mm or less, more preferably 1 μm or more and 3 mm or less,with 5 μm or more and 1 mm or less being further preferable.

The negative electrode layer can be produced by a known method. Forexample, it can be produced by a coating method, an electrostatic method(electrostatic spray method, electrostatic screen method, etc.).

(2) Electrolyte Layer

The electrolyte layer is a layer that comprises a solid electrolyte or alayer produced from a solid electrolyte. Although no specificrestrictions are imposed on the solid electrolyte, the solid electrolyteis preferably the sulfide solid electrolyte according to the invention.

The electrolyte layer may consist only of the solid electrolyte, and mayfurther comprise a binder. As the binder, the same binder as that usedin the negative electrode mix of the invention can be used.

It is preferred that the thickness of the electrolyte layer be 0.001 mmor more and 1 mm or less.

The solid electrolyte of the electrolyte layer may be fused. Fusionmeans that part of the solid electrolyte particles are dissolved and thedissolved part is integrated with other solid electrolyte particles.Further, the electrolyte layer may be a plate-like body of the solidelectrolyte, and as for the plate-like body, there may be cases wherepart or all of the solid electrolyte particles are dissolved to form aplate-like body.

The electrolyte layer can be produced by a known method. For example, itcan be produced by a known method. For example, it can be produced by acoating method or an electrostatic method (electrostatic spray method,electrostatic screen method, etc.).

(3) Positive Electrode Layer

The positive electrode layer is a layer that comprises a positiveelectrode active material. Preferably, the positive electrode layer is alayer that comprises the positive electrode mix of the invention or alayer that is produced from the positive electrode mix of the invention.

It is preferred that the thickness of the positive electrode layer be0.01 mm or more and 10 mm or less.

The positive electrode layer can be produced by a known method. Forexample, it can be produced by a coating method, an electrostatic method(electrostatic spray method, electrostatic screen method, etc.).

(4) Current Collector

The lithium ion battery of this embodiment preferably further comprisesa current collector. For example, a negative electrode current collectoris provided on the side opposite to the electrolyte layer side of thenegative electrode layer and a positive electrode current collector isprovided on the side opposite to the electrolyte layer side of thepositive electrode layer.

As the current collector, a plate-like body or a foil-like body, etc.formed of copper, magnesium, stainless steel, titanium, iron, cobalt,nickel, zinc, aluminum, germanium, indium, lithium or an alloy thereof,or the like.

The lithium ion battery of this embodiment can be produced by laminatingand bonding the above-mentioned elements. As the method for bonding, amethod in which the elements are stacked, pressurized and crimpled, amethod in which the elements are pressurized by passing through the tworolls (roll-to-roll method) or the like can be given.

Bonding may be conducted with an active material having an ionicconductivity or an adhesive material that does not impair ionicconductivity being present on the bonding surface.

In the bonding, heat sealing may be conducted within a range that thecrystal structure of the solid electrolyte is not changed.

The lithium ion battery of this embodiment can also be produced byforming the elements mentioned above in sequence. It can be produced bya known method. For example, it can be produced by a coating method, anelectrostatic method (electrostatic spray method, electrostatic screenmethod, etc.).

EXAMPLES

Hereinbelow, the invention will be explained in more detail inaccordance with the Examples.

The evaluation method is as follows.

(1) Measurement of Ionic Conductivity and Electron Conductivity

The sulfide solid electrolyte prepared in each example was filled in atablet molding machine and a pressure of 407 MPa (press indication value22 MPa) was applied by using a mini press machine to obtain a moldedbody. As the electrode, a carbon was put on the both sides of the moldedbody, and a pressure was applied again by a tablet molding machine,whereby a molded body for measurement (diameter: about 10 mm, thickness:0.1 to 0.2 cm) was prepared. For this molded body, an ionic conductivitywas measured by AC impedance measurement. The numerical value at 25° C.was adopted as the ionic conductivity value.

In the ionic conductivity measuring method used in this example, whenthe ionic conductivity is less than 1.0×10⁻⁶ S/cm, ionic conductivitywas determined to be unmeasurable since it cannot be measuredaccurately.

Further, the electron conductivity of this molded body was measured bydirect current electric measurement. As for the value of the electronconductivity, a numerical value at 25° C. was adopted. When the electronconductivity when a voltage of 5 V was applied was less than 1.0×10⁻⁶S/cm, the electron conductivity was determined to be unmeasurable.

(2) X-Ray Diffraction (XRD) Measurement

A circular pellet having a diameter of 10 mm and a height of 0.1 to 0.3cm was molded from the powder of the sulfide solid electrolyte producedin each example to prepare a sample. This sample was measured withouttouching the air using an air-tight holder for XRD. The 2θ position ofthe diffraction peak was determined by the centroid method using an XRDanalysis program JADE.

Measurement was conducted under the following conditions using a powderX-ray diffractormeter SmartLab manufactured by Rigaku Corporation.

Tube voltage: 45 kVTube current: 200 mAX-ray wavelength: CuKα rays (1.5418 Å)Optical system: Parallel beam systemSlit configuration: Solar slit 5°, incident slit: 1 mm, light receivingslit: 1 mmDetector: Scintillation counterMeasurement range: 2θ=10-60 degStep width, scan speed: 0.02 deg, 1 deg/min

In the analysis of the peak position for confirming the existence of thecrystal structure from the measurement result, the peak position wasobtained by drawing the baseline by cubic approximation using the XRDanalysis program JADE.

The intensity and the area of the diffraction peaks, i.e. a diffractionpeak at 2θ=25.2±0.5 deg (diffraction peak A) and 2θ=29.7±0.5 deg(diffraction peak B) were analyzed by the following procedures, wherebythe area ratio was calculated.

In an XRD pattern, the maximum peak position of 2θ=23 to 27 deg wasobtained, and the intensity (height) of the peak top thereof was takenas the intensity I_(A) of the diffraction peak. The integrated value ofthe actual measured intensity of 41 points which are within ±0.4 degreesfrom the maximum peak position was taken as the area S_(A) of thediffraction peak A. Similarly, the maximum peak position of 2θ=28 to 32deg was obtained, and the integrated value of the actually measuredintensity of 41 points which are within ±0.4 deg from the maximum peakposition was taken as the area S_(B) of the diffraction peak B. FromS_(A) and S_(B), the area ratio (S_(A)/S_(B)) was calculated.

As for the intensity I_(C) of the diffraction peak of lithium halide,when lithium halide is LiCl, a peak at 2θ=34.0 to 35.5 deg is specified,and the intensity of the peak top was taken as the intensity I_(C) ofthe diffraction peak. If two or more peaks appeared in this range, theintensity of the peak specified at the highest angle side was used. Whenlithium halide is LiBr, a peak at 2θ=32.5 to 33.9 deg was specified, andthe intensity of the peak top was taken as the intensity I_(C) of thediffraction peak. If two or more peaks appeared in this range, theintensity of the peak specified at the lowest angle side was used.

Further, a peak at 2θ=14.0 to 15.0 deg a specified, and the intensity ofthe peak top was taken as the intensity I^(D) of the diffraction peak.

(3) ICP Measurement

Powders of the sulfide solid electrolyte prepared in each example wereweighed and collected in a vial bottle in an argon atmosphere. A KOHalkaline aqueous solution was placed in the vial bottle, and the samplewas dissolved while paying attention to the collection of the sulfurcontent, and the solution was appropriately diluted, thereby to preparea measurement solution. This solution was measured with a Paschen Rungetype ICP-OES apparatus (SPECTRO ARCOS manufactured by SPECTRO), and thecomposition was determined.

A calibration solution for Li, P and S was prepared by using a 1000 mg/Lstandard solution for ICP measurement, and a calibration solution for Cland Br was prepared by using a 1000 mg/L standard solution for ionchromatography.

Two measurement solutions were prepared for each sample, fivemeasurements were performed for each measurement solution, and anaverage value was calculated. The composition was determined by theaverage of the measurement values of the two measurement solutions.

(4) Lattice Constant of the Argyrodite Type Crystal Structure

The XRD was measured under the same conditions as those mentioned in (2)above. The obtained XRD pattern was analyzed by the whole patternfitting (WPF) using crystal structure analysis software JADE ver 6manufactured by MDI, and each crystal component contained in the XRDpattern was specified, whereby the lattice constant of each componentwas calculated.

Removal of Background of the XRD Pattern

In an XRD pattern after the measurement, scattered light derived from adevice or signals derived from an air-tight holder are present on thelow angle side. In order to remove such signals, in conformity with theXRD pattern, a baseline attenuated from the low angle side wascalculated by 3D approximation.

Identification of Peak Components

For each component contained in the sample, a pattern calculated fromthe structure information on the inorganic crystal structure database(ICSD) was superimposed on the XRD pattern, whereby the peak componentwas identified. The structure information used is shown in Table 1.

Tabte 1 Component ICSD Crystal system Lattice constant (Å) Lithium#657596 Cubic system a = 5.723 sulfide Fm-3m(225) Lithium #418525 Cubicsystem a = 5.146 chloride Fm-3m(225) Lithium #27982 Cubic system a =5.500 bromide Fm-3m(225) Argyrodite #418490 Cubic system a = 9.859 (WithCl) F-43m(216) Argyrodite #421130 Cubic system a = 9.9926 (Without Cl)F-43m(216) Argyrodite #418488 Cubic system a = 9.988 (With Br)F-43m(216)

WPF Analysis

The main parameter settings for the WPF analysis are shown below.

X-ray wavelength: CuKα rays (λ=1.54184 Å)

Fitting parameter: The peak shape was approximated as a symmetricalpeak. Temperature factors were excluded from fitting. When crystals suchas Li₂S remain as fine peaks, the fitting may not converge in somecases. In such a case, structures other than the argyrodite typecrystals and the lithium halide crystals were excluded from the fittingobjects, and the half width and the intensity were manually input toconduct fitting, thereby to calculate the lattice constant of theargyrodite type crystal.

Regarding the lattice constant, it was confirmed whether the peakposition of the crystal structure to be evaluated was in good agreementwith the fitting results. Regarding the area ratio, it was a measure ofthe adequacy of the results that the R value was 10% or less. As for theR value serving as a measure of the accuracy of the fitting, the R valuemay become high when a large number of unknown peaks is present oramorphous peaks remain.

(5) Solid ³¹P-NMR Measurement

Approximately 60 mg of the powder sample was filled in an NMR sampletube, and solid ³¹P-NMR spectrum was obtained under the followingapparatus and conditions.

Apparatus: ECZ 400 R apparatus (manufactured by JEOL Ltd.)Observation nucleus: ³¹PObservation frequency: 161.944 MHzMeasurement temperature: Room temperaturePulse sequence: Single pulse (using 90° pulse)90° pulse width: 3.8μWaiting time after FID measurement until the next pulse application: 300sRotational speed of magic angle rotation: 12 kHzNumber of integrations: 16

Measurement range: 250 ppm to −150 ppm

In measurement of the solid ³¹P-NMR spectrum, the chemical shift wasobtained by using (NH₄)₂HPOi (chemical shift 1.33 ppm) as an externalreference.

NMR signals in the range of 78 to 92 ppm of the solid ³¹P-NMR spectrumwere separated into Gauss function or Pseudo-Voigt function (linear sumof Gauss function and Lorentz function) by the nonlinear least squaresmethod. In the above range, in addition to a peak derived from theargyrodite type crystal structure containing chlorine and bromine, apeak derived from Li₇PS₆ may appear at 88.5 to 90.5 ppm, and a peakderived from β crystals of Li₃PS₄ may appear at 86 to 87.6 ppm in anoverlapped manner. Therefore, wave separation was conducted by differentmethods for two cases, i.e. a case where these two peaks are notobserved and a case where these two peaks are observed.

(5-1) A Case where a Peak Derived from Li₇PS₆ and β Crystals of Li₃PS₄is not Observed

NMR signals in a range of 78 to 92 ppm were separated into four Gaussianfunctions or Pseudo-Voigt functions (linear sum of Gaussian function andLorentz function) in a range of the position and half width shown inTable 2 by the nonlinear least squares method. The area ratio (%) ofeach peak was calculated from the respective areas S₁ to S₄ of the peaksof the obtained A to C and the total S_(a11) (=S₁+S₂+S₃+S₄) thereof.

TABLE 2 Function Chemical shift Half width used for (ppm) (Hz)separation Area Fourth peak (P₄) 87.2-89.4 300-600 Pseudo-Voigt S₄ Thirdpeak (P₃) 85.2-86.7 150-800 Gauss S₃ Second peak (P₂) 83.2-84.7 150-800Gauss S₂ First peak (P₁) 81.5-82.5 150-500 Pseudo-Voigt S₁(5-2) A Case where a Peak Derived from Li₇PS₆ or β Crystals of Li₃PS₄ isObserved

As shown in Table 3, in addition to the four peaks derived from theargyrodite type crystal structure containing chlorine, the NMR signalsof 78 to 92 ppm were separated by the non-linear least square method byusing peak derived from Li₇PS₆ (peak I) or Li₃PS₄ (peak II). The arearatio (%) of each peak was calculated from the areas S₁ to S₄ of thepeaks A to C obtained, the areas b₁ and b₂ of the peaks I and II, andthe total of these S_(all+b)(−=S₁+S₂+S₃+S₄+b₁+b₂).

TABLE 3 Function Chemical shift Half width used for (ppm) (Hz)separation Area Fourth peak (P₄) 87.2-89.4 300-600 Pseudo-Voigt S₄ Thirdpeak (P₃) 85.2-86.7 150-800 Gauss S₃ Second peak (P₂) 83.2-84.7 150-800Gauss S₂ First peak (P₁) 81.5-82.5 150-500 Pseudo-Voigt S₁ Peak I88.5-90.5 150-800 Pseudo-Voigt b₁ Peak II 86.0-87.6 150-500 Pseudo-Voigtb₂

Production Example 1 (Production of Lithium Sulfide (Li₂S))

In a 500 mL-separable flask equipped with a stirrer, 200 g of LiOHanhydride (manufactured by Honjo Chemical Co., Ltd.) dried under aninert gas was charged. The temperature was raised under a nitrogenstream, and the internal temperature was maintained at 200° C. Thenitrogen gas was switched to hydrogen sulfide gas (Sumitomo Seika), theflow rate was allowed to be 500 mL/min, and LiOH anhydride was reactedwith hydrogen sulfide.

Moisture generated by the reaction was condensed by a condenser andrecovered. When the reaction was carried out for 6 hours, 144 mL ofwater was recovered. The reaction was continued further for 3 hours, butno water generation was observed.

The product powder was recovered and purity and XRD were measured. As aresult, the purity was 98.5%, and in XRD, the peak pattern of Li₂S wasconfirmed.

Example 1

Li₂S (purity: 98.5%) produced on Production Example 1, phosphoruspentasulfide (P₂S₅ manufactured by Thermophos International, purity:99.9% or more), lithium chloride NCI manufactured by Sigma Aldrich Co.,purity: 99%) and lithium bromide (LiBr manufactured by Sigma AldrichCo., purity: 99%) were used as starting materials (hereinafter, thepurity of each starting material was the same in all Examples). The rawmaterials were mixed such that the molar ratio of Li₂S, P₂S₅, LiCl andLiBr (Li₂S:P₂S₅:LiCl:LiBr) became 1.9:0.5:1.0:0.6. Specifically, 0.447 gof Li₂S, 0.569 g, 0.217 g and 0.267 g were mixed to obtain a rawmaterial mixture.

The raw material mixture and 30 g of zirconia balls having a diameter of10 mm were placed in a zirconia pot (45 mL) of a planetary ball mill(manufactured by Fritsch Co, Ltd., model No. P-7) and completely sealed.The inside of the pot was allowed to be an argon atmosphere. The rawmaterial mixture was treated (mechanical milling) for 15 hours with aplanetary ball mill (number of revolutions: 370 rpm), whereby glassypowder (intermediate) was obtained.

Approximately 1.5 g of the above-mentioned intermediate powder waspacked in a Tammann tube (PT2, manufactured by Tokyo Glass InstrumentsCo., Ltd.) in a glove box under an argon atmosphere, and the mouth ofthe Tammann tube was closed with a quartz wool, and the container wasfurther sealed with a SUS container to prevent intrusion of air.Thereafter, the sealed container was set in an electric furnace(FUW243PA, manufactured by AdvanTech Co., Ltd.) and heat-treated at arate of 2.5° C./min from room temperature to 430° C. (increased to 430°C. in about 3 hours), maintained at 430° C. for 8 hours, followed byslow cooling to obtain a sulfide solid electrolyte.

The ionic conductivity (σ) of the sulfide solid electrolyte was 13.0mS/cm.

An XRD pattern of the sulfide solid electrolyte is shown in FIG. 3. Apeak derived from the argyrodite type crystal structure was observed at2θ=15.5, 17.9, 25.4, 29.9, 31.3, 44.9, 47.8, 52.4 and 59.1 deg.

An ICP analysis was conducted for the sulfide solid electrolyte, and themolar ratio of each element was measured. As a result, the molar ratio a(Li/P) was 5.35, the molar ratio b (S/P) was 4.33, the molar ratio c(Cl/P) was 1.102, and the molar ratio d (Br/P) was 0.62.

The blending and production conditions of the raw materials are shown inTable 4. The molar ratio of each element in the raw material and themolar ratio of each element in the sulfide solid electrolyte are shownin Table 5. For the sulfide solid electrolyte, the areas and the arearatio of the diffraction peaks A and B in the XRD pattern and ionicconductivity σ are shown in Table 6. The intensity of the diffractionpeak and the intensity ratio of the diffraction peak in the XRD patternof the sulfide solid electrolyte are shown in Table 7. The latticeconstant and the area ratio of the ³¹P-NMR of the sulfide solidelectrolyte are shown in Table 8.

TABLE 4 Amount of raw materials blended (g) Amount of raw materialsNumber of Amount of raw materials blended (g) Revolutions blended (g)Li₂S P₂S₅ LiCl LiBr Apparatus (rpm) Time (h) Temperature (° C.) Time (h)Atmosphere Ex. 1 0.447 0.569 0.217 0.267 Ball mill 370 15 430 8 Ar Comp.Ex. 1 0.447 0.569 0.217 0.267 Manual mixing — — 430 8 Ar Ex. 2 7.75 9.873.76 4.63 Twin-screw kneader — — 430 8 Ar Ex. 3 0.421 0.537 0.123 0.419Ball mill 370 15 430 8 Ar Ex. 4 0.434 0.552 0.169 0.345 Ball mill 370 15430 8 Ar Ex. 5 0.461 0.587 0.269 0.183 Ball mill 370 15 430 8 Ar Ex. 60.476 0.606 0.324 0.095 Ball mill 370 15 430 8 Ar Ex. 7 0.479 0.6100.335 0.076 Ball mill 370 15 430 8 Ar Comp. Ex. 2 0.479 0.610 0.3350.076 Ball mill 370 15 500 8 Ar Comp. Ex. 3 0.581 0.611 0.252 0.057 Ballmill 370 15 430 8 Ar Comp. Ex. 4 0.593 0.574 0.109 0.224 Ball mill 37015 430 8 Ar

TABLE 5 Composition Elemental ratio of ratio of raw materials sulfidesolid electrolyte Li/P Li/P X*/P Cl/P Br/P Li/P Li/P X*/P Cl/P Br/P Ex.1 5.4 4.4 1.6 1.0 0.6 5.35 4.33 1.64 1.02 0.62 Comp. Ex. 1 5.4 4.4 1.61.0 0.6 5.30 4.20 1.60 1.01 0.59 Ex. 2 5.4 4.4 1.6 1.0 0.6 5.41 4.391.65 1.04 0.61 Ex. 3 5.4 4.4 1.6 0.6 1.0 5.40 4.42 1.60 0.61 0.99 Ex. 45.4 4.4 1.6 0.8 0.8 5.40 4.41 1.61 0.82 0.79 Ex. 5 5.4 4.4 1.6 1.2 0.45.40 4.38 1.62 1.21 0.41 Ex. 6 5.4 4.4 1.6 1.4 0.2 5.40 4.35 1.64 1.420.22 Ex. 7 5.4 4.4 1.6 1.44 0.16 5.40 4.39 1.63 1.45 0.18 Comp. Ex. 25.4 4.4 1.6 1.44 0.16 5.40 4.31 1.61 1.44 0.17 Comp. Ex. 3 5.8 4.8 1.21.08 0.12 5.80 4.70 1.23 1.08 0.15 Comp. Ex. 4 6.0 5.0 1.0 0.5 0.5 6.005.05 1.02 0.51 0.51 *X is the total of Cl and Br.

TABLE 6 Diffraction peak area Ionic and area ratio conductivity S_(A)S_(B) S_(A)/S_(B) (mS/cm) Ex. 1 311496 332792 0.936 13.0 Comp. Ex. 1355834 435918 0.816 3.7 Ex 2 322317 345101 0.934 13.5 Ex. 3 391148386904 1.011 12.3 Ex. 4 350789 358147 0.979 12.8 Ex. 5 266841 3018130.884 12.1 Ex. 6 275176 317723 0.866 12.1 Ex. 7 257130 302562 0.850 10.5Comp. Ex. 2 190978 248258 0.769 6.3 Comp. Ex. 3 265408 314342 0.844 6.0Comp. Ex. 4 424826 497569 0.927 4.9

In the table, S_(A) is an area of the diffraction peak A (2θ=25.2±0.5deg) and S_(B) is an area of the diffraction peak B (29.7±0.5 deg),

TABLE 7 Diffraction peak intensity Intensity ratio I_(A) I_(C) I_(D)I_(C)/I_(A) I_(D)/I_(A) Ex. 1 17994 640 ND 0.036 — Comp. Ex. 1 17835 801ND 0.045 — Ex. 2 20687 968 ND 0.044 — Ex. 3 24086 1076 ND 0.045 — Ex. 421821 ND ND — — Ex. 5 16476 648 ND 0.039 — Ex. 6 15855 627 ND 0.042 —Ex. 7 15855 787 ND 0.050 — Comp. Ex. 2 12315 1521 1218 0.124 0.099 Comp.Ex. 3 16135 686 ND 0.043 — Comp. Ex. 4 25031 626 ND 0.025 —

In the table, I_(A) is an intensity of the diffraction peak A(2θ=25.2±0.5 deg), I_(C) is the total of intensities of the diffractionpeaks derived from lithium halide, and I_(D) is an intensity of thediffraction peak D (2θ=14.4±0.5 deg).

TABLE 8 Lattice constant Peak area ratio of P-NMR (%) (Å) P1 P2 P3 P4P1 + P2 Ex. 1 9.877 19.9 46.9 18.5 14.7 66.8 Comp. Ex. 1 9.923 — — — — —Ex. 2 9.876 20.8 44.5 20.7 13.9 65.4 Ex. 3 9.918 18.6 44.4 21.3 15.763.0 Ex. 4 9.900 18.5 43.8 29.8 7.9 62.3 Ex. 5 9.881 25.0 39.9 27.9 7.264.9 Ex. 6 9.820 40.8 34.7 19.4 5.1 75.5 Ex. 7 9.826 39.9 36.8 18.9 4.476.7 Comp. Ex. 2 9.884 8.2 29.8 29.7 32.4 38.0 Comp. Ex. 3 9.880 28.124.0 25.6 22.3 52.1 Comp. Ex. 4 9.915 9.2 22.0 40.3 28.5 31.2

Comparative Example 1

The same raw materials as in Example 1 was placed in a Schlenk bottleand shaken by hands to mix. The obtained raw material mixture washeat-treated at 430° C. for 8 hours in the same manner as in Example 1to obtain a sulfide solid electrolyte.

The sulfide solid electrolyte was evaluated in the same manner as inExample 1. The results are shown in Tables 5 to 8.

In Comparative Example 1, it is assumed that, since mixing of the rawmaterials before the heat treatment was not sufficient, halogen was notdispersed by the heat treatment, and as a result, incorporation of ahalogen into the site of the argyrodite crystal structure becameinsufficient.

Example 2

In Example 2, a twin-screw kneader was used instead of the planetaryball mill in Example 1 for the preparation of an intermediate. Kneadingby using the twin screw kneader was specifically conducted as follows.

A feeder (manufactured by Aisin Nanotechnologies Co., Ltd., microfeeder)and a twin-screw kneading extruder (manufactured by Kuritomo Ltd., KRCkneader, paddle diameter φ 8 mm) were installed in a glove box. Amixture of 3.76 g of LiCl, 4.63 g of LiBr, 7.75 g of Li₂S and 9.87 g ofP₂S₅ was fed at a constant speed from a supply port, and kneading wasconducted at a revolution number of 150 rpm at a temperature of 250° C.(measured with a thermometer at the outer surface of the casing of thetwin-screw kneading extruder). The powder was discharged from thekneader outlet in about 120 minutes. The discharged powder was returnedto the supply port again and kneading was repeated 5 times. The reactiontime was about 10 hours in total.

The resulting intermediate was heat-treated at 430° C. for 8 hours inthe same manner as in Example 1, by which a sulfide solid electrolytewas obtained.

The resulting sulfide solid electrolyte was evaluated in the same manneras in Example 1. The results are shown in Tables 5 to 8.

Since the twin-screw kneading extruder used for mixing the raw materialsis a device that can mix the materials to a significantly high degree,it is assumed that constituent elements were highly dispersed in theintermediate. It may be assumed that the ionic conductivity was improvedas a result.

Examples 3 to 7 and Comparative Examples 2 to 4

Sulfide solid electrolytes were prepared and evaluated in the samemanner as in Example 1, except that the raw material composition waschanged as shown in Table 4. The results are shown in Tables 5 to 8.

In Comparative Example 2, it is considered that a halogen which hadoccupied the site in the crystal structure was removed due to a highheat treatment temperature. Cl present in the 4a site or Br present inthe 4d site are easily removed from the site.

An XRD pattern of the sulfide solid electrolyte prepared in ComparativeExample 2 is shown in FIG. 4.

Since the crystals of lithium halide and novel crystals havingdiffraction peaks at 2θ=14.4±0.5 deg and 33.8±0.5 deg are present, it isassumed that part of Cl or Br that had occupied the site of theargyrodite crystal structure was removed and these crystals were formed.

As a result of an XRD measurement of the sulfide solid electrolyteobtained in each example, a peak derived from the argyrodite crystalstructure was observed.

Examples 8 to 12 and Comparative Example 5

Sulfide solid electrolytes were prepared and evaluated in the samemanner as in Example 1, except that blending of the raw materials andproduction conditions were changed as shown in Table 9. The results areshown in Tables 10 to 12. As a result of an XRD measurement of thesulfide solid electrolyte obtained in each example, a peak derived fromthe argyrodite crystal structure was observed.

TABLE 9 MM treatment conditions Amount of raw materials Number of Heattreatment conditions blended (g) revolutions Time Temperature Time Li₂SP₂S₅ LiCl LiBr (rpm) (H) Atmosphere (° C.) (H) Ex. 8 0.476 0.606 0.3240.095 370 48 Ar 440 4 Ex. 9 0.461 0.587 0.269 0.183 370 48 Ar 430 4 Ex.10 0.447 0.569 0.217 0.267 370 48 Ar 420 4 Ex. 11 0.434 0.552 0.1690.345 370 48 Ar 430 4 Ex. 12 0.421 0.537 0.123 0.419 370 48 Ar 430 4 Ex.13 0.436 0.569 0.228 0.267 370 48 H₂S 500 4 Ex. 14 2.980 3.794 1.4471.779 — — Ar 430 4 Ex. 15 2.980 3.794 1.447 1.779 — — Ar 430 48 Comp.0.614 0.595 0.166 0.125 370 48 Ar 500 10 Ex. 5

TABLE 10 Composition ratio Elemental ratio of raw materials of sulfidesolid electrolyte Li/P Li/P X*/P Cl/P Br/P Li/P Li/P X*/P Cl/P Br/P Ex.8 5.4 4.4 1.6 1.40 0.20 5.40 4.40 1.592 1.39 0.20 Ex. 9 5.4 4.4 1.6 1.200.40 5.40 4.40 1.61 1.20 0.41 Ex. 10 5.4 4.4 1.6 1.00 0.60 5.40 4.401.61 1.01 0.60 Ex. 11 5.3 4.3 1.6 0.80 0.80 5.30 4.30 1.60 0.79 0.81 Ex.12 5.4 4.4 1.6 0.60 1.00 5.40 4.40 1.60 0.60 1.00 Ex. 13 5.4 4.4 1.71.05 0.60 5.35 4.40 1.64 1.04 0.60 Ex. 14 5.4 4.4 1.6 1.00 0.60 5.404.40 1.61 1.00 0.61 Ex. 15 5.4 4.4 1.6 1.00 0.60 5.40 4.40 1.59 0.990.60 Comp. Ex. 5 6.0 5.0 1.0 0.75 0.25 6.00 4.90 1.04 0.75 0.29 *X isthe total of Cl and Br.

TABLE 11 Diffraction peak area Ionic and area ratio conductivity S_(A)S_(B) S_(A)/S_(B) (mS/cm) Ex. 8 286065 311612 0.918 11.5 Ex. 9 277622301813 0.920 12.5 Ex. 10 298354 310616 0.961 13.0 Ex. 11 374902 4015530.934 9.1 Ex. 12 362284 366129 0.989 8.8 Ex. 13 311222 352218 0.884 11.8Ex. 14 340817 369344 0.923 10.5 Ex. 15 320708 348913 0.919 12.1 Comp.Ex. 5 429022 503469 0.852 5.1

In the table, S_(A) is the area of the diffraction peak A (2θ=25.2±0.5deg) and S_(B) is the area of the diffraction peak B (29.7±0.5 deg).

TABLE 12 Lattice constant Peak area ratio of P-NMR (%) (Å) P1 P2 P3 P4P1 + P2 Ex. 8 9.825 39.2 36.3 20.4 4.2 75.5 Ex. 9 9.857 24.3 41.3 29.05.4 65.6 Ex. 10 9.874 40.6 33.3 17.2 8.9 73.9 Ex. 11 9.905 26.3 48.915.1 9.7 75.2 Ex. 12 9.917 18.6 44.3 21.6 15.5 62.9 Ex. 13 9.863 27.938.4 19.8 13.8 66.4 Ex. 14 9.881 20.5 44.9 20.1 14.5 65.4 Ex. 15 9.87724.6 45.6 17.7 12.1 70.2 Comp. Ex. 5 9.921 24.2 34.6 36.0 5.2 58.8

Example 13

An intermediate was prepared in the same manner as in Example 1, exceptthat the raw material composition and the production conditions werechanged as shown in Table 9.

In a glove box in an atmosphere of argon, about 1.5 g of powder of theintermediate was filled in a glass tube provided with sealing function.In order to prevent intrusion of air, the front end of the glass tubewas sealed with a dedicated jig. Thereafter, the glass tube was set inan electric furnace. The dedicated jig was inserted into a joint in theelectric furnace, and was connected with a glass circulation tube. Aheat treatment was conducted while circulating hydrogen sulfide at aflow rate of 0.5 L/min. Specifically, the temperature was elevated fromroom temperature to 500° C. at a rate of 3° C./min, and retained at 500°C. for 4 hours. Thereafter, the glass tube was gradually cooled, bywhich a sulfide solid electrolyte was obtained.

The resulting solid electrolyte was evaluated in the same manner as inExample 1. The results are shown in Tables 10 to 12, The sulfide solidelectrolyte obtained in Example 13 also had an electron conductivity ofless than 10⁻⁶ S/cm. As a result of an XRD measurement, a peak derivedfrom the argyrodite crystal structure was observed.

Example 14

In the same manner as in Example 2, kneading by using a twin-screwkneader was conducted for preparation of an intermediate. The kneadingby using a twin-screw kneader was specifically conducted in the samemanner as in Example 2, except that a mixture of 1.447 g of LiCl, 1.779g of LiBr, 2.980 g of Li₂S, and 3.794 g of P₂S₅ was supplied at aconstant speed from a supply part by a feeder, by which an intermediatewas obtained.

The resulting intermediate was heat-treated at 430° C. for 4 hours, bywhich a sulfide solid electrolyte was obtained.

The results of evaluation of the resulting sulfide solid electrolyte areshown in Tables 10 to 12.

The sulfide solid electrolyte obtained in Example 14 had an electronconductivity of less than 10⁻⁶ S/cm. As a result of an XRD measurement,a peak derived from the argyrodite crystal structure was observed.

Example 15

The sulfide solid electrolyte was prepared and evaluated in the samemanner as in Example 14, except that the preparation conditions werechanged as shown in Table 9. The results are shown in Tables 10 to 12.

The sulfide solid electrolyte obtained in Example 15 had an electronconductivity of less than 10⁻⁶ S/cm. As a result of an XRD measurement,a peak derived from the argyrodite crystal structure was observed.

[Amount of Hydrogen Sulfide Generated from Sulfide Solid Electrolyte]

The amount of hydrogen sulfide generated from the sulfide solidelectrolytes prepared in Example 10 and Comparative Example 4 wasevaluated by using the apparatus shown in FIG. 5. This apparatuscomprises a flask 1 for humidifying air, a flask 2 equipped with atemperature/hygrometer 6 for measuring the temperature and humidity ofhumidified air, a Schlenk bottle 3 for charging the measurement sample4, and a hydrogen sulfide measuring device 7 for measuring theconcentration of hydrogen sulfide contained in humidified air areconnected in this order through a pipe. The evaluation procedure is asfollows.

About 0.1 g of powder sample prepared by sufficiently pulverizing thesample in a nitrogen glow box at a dew point of −80° C. was weighed andput in the 100 ml-Schlenk bottle 3, and the bottle was sealed (numericalreference 4 in FIG. 5).

Subsequently, air was flown into the flask 1 at 500 mL/min. The flowrate of air was measured with a flowmeter 5. Air was passed throughwater in the flask 1 and humidified, Subsequently, humidified air wasflown into the flask 2, and the temperature and humidity of the air weremeasured. Immediately after the start of distribution the temperature ofthe air was 25° C. and the humidity was 80 to 90%. Thereafter,humidified air was caused to flow through the Schlenk bottle 3 andbrought into contact with the measurement sample 4. Humidified aircirculated in the Schlenk bottle 3 was passed through a hydrogen sulfidemeasuring device 7 (Model 3000 RS manufactured by AMI), and the amountof hydrogen sulfide contained in the humidified air was measured. Themeasurement time was set to be from immediately after air circulation to1 hour after circulation. The amount of hydrogen sulfide was recorded atintervals of 15 seconds.

From the total amount of hydrogen sulfide observed in 2 hours, thehydrogen sulfide generation amount (mg/g) per 1 g of the sample wascalculated. As a result, the amount of the generated hydrogen sulfidewas 26 mg/g for the sulfide solid electrolyte of Example 10 and was 64mL/g for the sulfide solid electrolyte of Comparative Example 4.

[Lithium Ion Battery]

Lithium ion batteries were produced by using the sulfide solidelectrolytes obtained in Example 13 and Comparative Example 1, and ratecharacteristics were evaluated.

(A) Production of Lithium Ion Battery

50 mg of the sulfide solid electrolyte obtained in Example 13 orComparative Example 1 was respectively put in a stainless steel moldhaving a diameter of 10 mm and flattened so that the layer thickness ofthe electrolyte layer became uniform, and then, a pressure of 185 MPawas applied from the upper surface of the electrolyte layer by means ofa hydraulic press machine, and pressure molding was conducted.

As the positive electrode active material, Li₄Ti₅O₁₂ coatedLiNi_(0.8)Co_(0.15)A_(l0.05)O₂ was mixed with the sulfide solidelectrolyte obtained in Example 13 or Comparative Example 1 in a ratioof 70:30 by weight to prepare a positive electrode material. 15 mg ofthe positive electrode material was put on the upper surface of theelectrolyte layer, flattened so that the layer thickness of the positiveelectrolyte layer became uniform, and then, a pressure of 407 MPa wasapplied from the upper surface of the electrolyte layer by means of ahydraulic press machine, and pressure molding was conducted.

Graphite powder as a negative electrode active material and the sulfidesolid electrolyte obtained in Example 13 or in Comparative Example 1were mixed at a ratio of 60:40 by weight to obtain a negative electrodematerial. 12 mg of the negative electrode material was put to the sideof the electrolyte layer opposite to the positive electrode layer, andflattened so that the layer thickness of the negative electrode layerbecame uniform, and then, a pressure of 555 MPa was applied from theupper surface of the negative electrode layer by means of a hydraulicpress machine, and pressure molding was conducted. As a result, alithium ion battery having a three-layer structure of the positiveelectrode, the solid electrolyte layer and the negative electrode wasprepared.

(B) Rate Characteristics Test

The lithium ion battery produced in (A) above was allowed to stand in athermostat set at 25° C. for 12 hours and then evaluated. At the firstcycle, charging was conducted to 4.2V at 0.1 C (0.189 mA) anddischarging was conducted to 3.1V at 0.1 C (0.189 mA), and at the secondcycle to the tenth cycle, charging was conducted to 4.2V at 0.5 C (0.945mA) and discharging was conducted to 3.1V at 0.5 C (0.945 mA). Thecapacity at the tenth cycle was measured. By using a separate batteryproduced with the same sample, the capacity at the tenth cycle wasmeasured when charging and discharging were conducted from the one cycleto the tenth cycle at 0.1 C. The ratio of capacity when charging anddischarging were conducted at 0.5 C and the capacity when charging anddischarging were conducted at 0.1 C was taken as the evaluation value ofthe rate characteristics. The rate characteristics of the lithium ionbattery obtained by using the sulfide solid electrolyte of Example 13was 73%. The rate characteristics in the lithium ion battery obtained byusing the sulfide solid electrolyte of Comparative Example 1 was 50%.

Evaluation Example

The sulfide solid electrolyte obtained in Example 1 was subjected tostructural analysis using synchrotron radiation and neutron.Specifically, X-ray diffraction using synchrotron radiation wasconducted on BL19B2 of SPring-8. The sample sealed in the glasscapillary was measured. Measured data was corrected by using a CeO₂standard sample. A Rietveld analysis was conducted based on thestructural model of the argyrodite crystals. Neutron diffraction wasmeasured at BL 20 of J-PARC. In the neutron diffraction, the occupationratio of each site which was distinguished from S and Cl of 4a and 4dsites by the Rietveld structure analysis can be calculated. From thestructural model that satisfies both the synchrotron radiation X-raydiffraction data and the neutron diffraction data, the occupation ratio,that is, the abundance ratio of the 4a and 4d sites was calculated.

FIG. 6 shows the results of the structural analysis by synchrotronradiation. It can be confirmed that the difference between the actuallymeasured data and the analysis data is small, and conformity of fittingis high. As a result of the analysis, as for the site selectivity of ahalogen, it can be confirmed that chloride (CI) tends to occupy the 4dsite and bromine (Br) tends to occupy the 4a site.

Although only some exemplary embodiments and/or examples of thisinvention have been described in detail above, those skilled in the artwill readily appreciate that many modifications are possible in theexemplary embodiments and/or examples without materially departing fromthe novel teachings and advantages of this invention. Accordingly, allsuch modifications are intended to be included within the scope of thisinvention.

The documents described in the specification and the specification ofJapanese application(s) on the basis of which the present applicationclaims Paris convention priority are incorporated herein by reference inits entirety.

1-20. (canceled)
 21. A sulfide solid electrolyte, comprising lithium,phosphorus, sulfur, chlorine and bromine, wherein a molar ratio of thechlorine to the phosphorus, c (Cl/P), and a molar ratio of the bromineto the phosphorus, d (Br/P), satisfy formula (1):1.2<c+d<1.9  (1), and wherein the sulfide solid electrolyte contains anargyrodite type crystal structure and a lattice constant of theargyrodite type crystal structure is 9.800 Å or more and 9.920 Å orless.
 22. The sulfide solid electrolyte according to claim 21, whereinin powder X-ray diffraction analysis using CuKα rays, the sulfide solidelectrolyte has a diffraction peak A at 2θ=25.2+0.5 deg and adiffraction peak B at 2θ=29.7+0.5 deg, the diffraction peak A and thediffraction peak B satisfy formula (A):0.845<S _(A) /S _(B)<1.200  (A) wherein S_(A) is an area of thediffraction peak A and S_(B) is an area of the diffraction peak B. 23.The sulfide solid electrolyte according to claim 21, wherein the molarratio of the bromine to the phosphorus, d (B/P), is 0.15 or more and 1.6or less.
 24. The sulfide solid electrolyte according to claim 21,wherein the molar ratio of the chlorine to the phosphorus, c (Cl/P), andthe molar ratio of the bromine to the phosphorus, d (Br/P), satisfyformula (2):0.08<d/(c+d)<0.8  (2).
 25. The sulfide solid electrolyte according toclaim 21, wherein a molar ratio of the lithium to the phosphorus, a(Li/P), a molar ratio of the sulfur to the phosphorus, b (S/P), themolar ratio of the chlorine to the phosphorus, c (Cl/P), and the molarratio of the bromine to the phosphorus, d (Br/P), satisfy formulas (3)to (5):5.0≤a≤7.5  (3)6.5≤a+c+d≤7.5  (4)0.5≤a-b≤1.5  (5) with the proviso that b>0, c≥0 and d>0.
 26. The sulfidesolid electrolyte according to claim 21, wherein, in powder X-raydiffraction analysis using CuKα rays, the sulfide solid electrolyte doesnot have a diffraction peak derived from lithium halide or, if thesulfide solid electrolyte has a diffraction peak derived from lithiumhalide, said diffraction peak satisfies formula (B):0<I _(C) /I _(A)<0.08  (B) wherein I_(C) is an intensity of adiffraction peak of lithium halide, and I_(A) is an intensity of adiffraction peak at 2θ=25.2±0.5 deg.
 27. The sulfide solid electrolyteaccording to claim 21, wherein, in powder X-ray diffraction analysisusing CuKα rays, the sulfide solid electrolyte does not have adiffraction peak at 2θ=14.4±0.5 deg and 33.8±0.5 deg or, if the sulfidesolid electrolyte has a diffraction peak at 2θ=14.4±0.5 deg and 33.8±0.5deg, said diffraction peak satisfies formula (C):0<I _(D) /I _(A)<0.09  (C) wherein I_(D) is an intensity of adiffraction peak at 2θ=44.4±0.5 deg and I_(A) is an intensity of adiffraction peak at 2θ=25.2±0.5 deg.
 28. The sulfide solid electrolyteaccording to claim 21, wherein in the solid ³¹P-NMR measurement, thesolid electrolyte has a peak at each of 81.5 to 82.5 ppm, 83.2 to 84.7ppm, 85.2 to 86.7 ppm and 87.2 to 89.4 ppm and the ratio of the sum ofthe area of the peak at 81.5 to 82.5 ppm and 83.2 to 84.7 ppm relativeto the total of all peaks that appear within a range of 78 to 92 ppm is60% or more.
 29. The sulfide solid electrolyte according to claim 21,wherein: in powder X-ray diffraction analysis using CuKα rays, thesulfide solid electrolyte has a diffraction peak A at 2θ=25.2+0.5 degand a diffraction peak B at 2θ=29.7±0.5 deg, the diffraction peak A andthe diffraction peak B satisfy formula (A):0.845<S _(A) /S _(B)<1.200  (A) wherein S_(A) is an area of thediffraction peak A and S_(B) is an area of the diffraction peak B: andthe molar ratio of the bromine to the phosphorus, d (B/P), is 0.15 ormore and 1.6 or less.
 30. The sulfide solid electrolyte according toclaim 21, wherein: in powder X-ray diffraction analysis using CuKα rays,the sulfide solid electrolyte has a diffraction peak A at 2θ=25.2±0.5deg and a diffraction peak B at 2θ=29.7±0.5 deg, the diffraction peak Aand the diffraction peak B satisfy formula (A):0.845<S _(A) /S _(B)<1.200  (A) wherein S_(A) is an area of thediffraction peak A and S_(B) is an area of the diffraction peak B: andthe molar ratio of the chlorine to the phosphorus, c(Cl/P), and themolar ratio of the bromine to the phosphorus, d (Br/P), satisfy formula(2):0.08<d/(c+d)<0.8  (2).
 31. The sulfide solid electrolyte according toclaim 21, wherein: in powder X-ray diffraction analysis using CuKα rays,the sulfide solid electrolyte has a diffraction peak A at 2θ=25.2±0.5deg and a diffraction peak B at 2θ=29.7±0.5 deg, the diffraction peak Aand the diffraction peak B satisfy formula (A):0.845<S _(A) /S _(B)<1.200  (A) wherein S_(A) is an area of thediffraction peak A and S_(B) is an area of the diffraction peak B: and amolar ratio of the lithium to the phosphorus, a (Li/P), a molar ratio ofthe sulfur to the phosphorus, b (S/P), the molar ratio of the chlorineto the phosphorus, c (CUP), and the molar ratio of the bromine to thephosphorus, d (Br/P), satisfy formulas (3) to (5):5.0≤a≤7.5  (3)6.5≤a+c+d≤7.5  (4)0.5≤a−b≤1.5  (5) with the proviso that b>0, c>0 and d>0.
 32. The sulfidesolid electrolyte according to claim 21, wherein: in powder X-raydiffraction analysis using CuKα rays, the sulfide solid electrolyte hasa diffraction peak A at 2θ=25.2±0.5 deg and a diffraction peak B at2θ=29.7±0.5 deg, the diffraction peak A and the diffraction peak Bsatisfy formula (A):0.845<S _(A) /S _(B)<1.200  (A) wherein S_(A) is an area of thediffraction peak A and S_(B) is an area of the diffraction peak B: andin powder X-ray diffraction analysis using CuKα rays, the sulfide solidelectrolyte does not have a diffraction peak derived from lithium halideor, if the sulfide solid electrolyte has a diffraction peak derived fromlithium halide, said diffraction peak satisfies formula (B):0<I _(C) /I _(A)<0.08  (B) wherein I_(C) is an intensity of adiffraction peak of lithium halide, and I_(A) is an intensity of adiffraction peak at 2θ=25.2±0.5 deg.
 33. The sulfide solid electrolyteaccording to claim 21, wherein: in powder X-ray diffraction analysisusing CuKα rays, the sulfide solid electrolyte has a diffraction peak Aat 2θ=25.2±0.5 deg and a diffraction peak B at 2θ=29.7±0.5 deg, thediffraction peak A and the diffraction peak B satisfy formula (A):0.845<S ₁ /S _(B)<1.200  (A) wherein S_(A) is an area of the diffractionpeak A and S_(B) is an area of the diffraction peak B: and in powderX-ray diffraction analysis using CuKα rays, the sulfide solidelectrolyte does not have a diffraction peak at 2θ=14.4±0.5 deg and33.8±0.5 deg or, if the sulfide solid electrolyte has a diffraction peakat 2θ=14.4±0.5 deg and 33.8±0.5 deg, said diffraction peak satisfiesformula (C):0<I _(D) /I _(A)<0.09  (C) wherein I_(D) is an intensity of adiffraction peak at 2θ=14.4±0.5 deg and I_(A) is an intensity of adiffraction peak at 2θ=25.2±0.5 deg.
 34. The sulfide solid electrolyteaccording to claim 21, produced by a process comprising: applying amechanical stress to raw materials to obtain an intermediate containinga glass component; heat-treating the intermediate.
 35. The sulfide solidelectrolyte according to claim 21, produced by a process comprising:applying a mechanical stress to raw materials to obtain an intermediatecontaining a glass component; and heat-treating the intermediate at atemperature of 350 to 480° C. in an inert gas atmosphere.
 36. Anelectrode mix, comprising: the sulfide solid electrolyte according toclaim 21; and an active material.
 37. A lithium ion battery, comprisingthe sulfide solid electrolyte according to claim
 21. 38. A lithium ionbattery, comprising the electrode mix according to claim 36.